Ultrathin, Molecular-Sieving Graphene Oxide Membranes for Separations Along with Their Methods of Formation and Use

ABSTRACT

Methods for forming an ultrathin GO membrane are provided. The method can include: dispersing a single-layered graphene oxide powder in deionized water to form a single-layered graphene oxide dispersion; centrifuging the graphene oxide dispersion to remove aggregated graphene oxide material from the single-layered graphene oxide dispersion; thereafter, diluting the single-layered graphene oxide dispersion by about ten times or more through addition of deionized water to the graphene oxide dispersion; and thereafter, passing the single-layered graphene oxide dispersion through a substrate such that a graphene oxide membrane is formed on the substrate. Filtration membranes are also provided and can include: a graphene oxide membrane having a thickness of about 1.8 nm to about 180 nm, with the graphene oxide membrane comprises about 3 to about 30 layers of graphene oxide flakes.

The present application claims priority to and is a continuation of U.S. patent application Ser. No. 14/180,724 titled “Ultrathin, Molecular-Sieving Graphene Oxide Membranes for Separations” of Yu, et al. filed on Feb. 14, 2014, and claims priority to U.S. Provisional Patent Application Ser. No. 61/850,415 titled “Ultrathin, Molecular-Sieving Graphene Oxide Membranes for Separations” of Yu, et al. filed on Feb. 14, 2013; the disclosures of which are incorporated by reference herein.

BACKGROUND

Microporous membranes, including zeolite membranes, silica membranes, carbon membranes, and microporous polymeric membranes, have shown excellent gas mixture separation performance and may have wide applications in many industrially important separation processes. Current microporous membranes, however, are usually thick (thickness greater than 20 nm) in order to minimize flux contribution through non-selective defects and maintain reasonable separation selectivity. Further reducing membrane thickness to sub-20 nm range to lower transport resistance without introducing extra non-selective defects is highly challenging for current microporous membranes. This challenge may result from the limitations of membrane materials and/or membrane preparation techniques.

Graphene-based materials, such as graphene and graphene oxide (GO), have been considered as a promising membrane material, because they are only one carbon atom thick, and thus may form the thinnest separation membranes to maximize flux. Besides, they have good stability and strong mechanical strength. However, these graphene-based materials have been found to be impermeable to small gas molecules. Extensive simulation studies, therefore, have been conducted to understand effects of various potential defects or artificially generated “holes” on permeation behaviors of molecules and to predict mixture separation performance. Very recently, others reported an etched graphene by UV-induced oxidation to create pores, and found that the transport rates of H₂ and CO₂ were 3 to 4 orders of magnitude higher than N₂ and CH₄ through porous graphene flakes.

However, no practical graphene-based separation membranes have been prepared for studying their separation potential for gas mixtures.

SUMMARY

Objects and advantages of the invention will be set forth in part in the following description, or may be obvious from the description, or may be learned through practice of the invention.

Methods are generally provided for forming an ultrathin GO membrane. In one embodiment, the method comprises: dispersing a single-layered graphene oxide powder in deionized water to form a single-layered graphene oxide dispersion; centrifuging the graphene oxide dispersion to remove aggregated graphene oxide material from the single-layered graphene oxide dispersion; thereafter, diluting the single-layered graphene oxide dispersion by about ten times or more through addition of deionized water to the graphene oxide dispersion; and thereafter, passing the single-layered graphene oxide dispersion through a substrate such that a graphene oxide membrane is formed on the substrate.

Filtration membranes, such as those formed according to the presently provided methods, are also provided. In one embodiment, the filtration membrane includes: a graphene oxide membrane having a thickness of about 1.8 nm to about 180 nm, with the graphene oxide membrane comprises about 3 to about 30 layers of graphene oxide flakes.

Other features and aspects of the present invention are discussed in greater detail below.

BRIEF DESCRIPTION OF THE DRAWINGS

A full and enabling disclosure of the present invention, including the best mode thereof to one skilled in the art, is set forth more particularly in the remainder of the specification, which includes reference to the accompanying figures, in which:

FIGS. 1A-1I show GO membranes supported on porous AAO, with FIG. 1A showing a digital picture of an ultrathin GO membrane on AAO (about 9 nm) with the middle open white area being the permeation area (˜4 cm²) with supported GO, and yellow tape is for GO protection and for sealing by O-ring during permeation measurements; FIG. 1B showing an AFM image of a GO flake on freshly cleaved mica; FIG. 1C showing the height profile across the line in FIG. 1B; FIG. 1D showing a FE-SEM image of the surface of a GO membrane (about 18-nm thick) on porous AAO; FIG. 1E showing a FE-SEM image of the GO membrane surface (about 18-nm thick) with higher magnification; FIG. 1F showing an AAO surface without GO membrane; FIG. 1G showing a FE-SEM image of the cross-sectional view of a thick GO membrane (about 180 nm) where the ulrathin GO membranes (1.8, 9, and 18 nm thick) were prepared by diluting GO filtration solution for the 180-nm thick membrane in (G) by 100, 20, and 10 times, while maintaining total filtration solution volume constant at 25 ml; FIG. 1H shows an A1 2P and FIG. 1 I shows a C 1S XPS spectra of ultrathin GO membranes (ca. 1.8, 9, and 18 nm thick) supported on porous AAO. The scale bars in FIG. 1B being 500 nm, in FIG. 1D being 5 μm, in FIGS. 1E and 1F being 100 nm; in FIG. 1G being 1 μm.

FIGS. 2A and 2B show single-gas permeation through GO membranes supported on porous AAO at 20° C., with FIG. 2A showing permeances of four molecules through an approximately 18-nm tick GO membrane and FIG. 2B showing permeances of H₂ and He through GO membranes with different thicknesses. The lines in FIG. 1B are exponential fits, which indicates permeances of H₂ and He decrease exponentially with membrane thickness, instead of expected inversely proportional to membrane thickness.

FIGS. 3A-3H show 50/50 H₂/CO₂ and H₂/N₂ mixture separation by ultrathin GO membranes and comparison with membranes in the literature for H₂/CO₂ mixture separation, with FIGS. 3A and 3B showing separation results for 1.8-nm thick GO membrane; FIGS. 3C and 3D showing separation results for 9-nm thick GO membrane; FIGS. 3E and 3F showing separation results for 18-nm thick GO membrane; and FIG. 3G shows a comparison of ultrathin GO membranes with polymeric membranes and inorganic microporous membranes for H₂/CO₂ mixture separation: selectivity versus H₂ permeance. The lowest line is the 2008 upper bound of polymeric membrane for H₂/CO₂, assuming membrane thickness is 1 μm. The points (1-11) are microporous inorganic membranes from literature, and the upper line is the proposed upper bound for inorganic membranes, based on these points (1-11). The points (12) circled with a dotted line are ultrathin GO membranes from this study. The table of FIG. 1H explains points (1-12). Comparison with polymeric membranes for H₂/N₂ mixture separation is presented in FIG. 10.

FIGS. 4A and 4B show absorbance curves for determination of the GO solution after centrifuge that uses UV-vis to measure the absorbance of the prepared GO standard solution (0, 0.02, 0.125, 0.25, 0.5, 1 and 2 mg/mL). It was found that the concentration of GO solution had an excellent linear fit with the UV absorbance, as shown in FIG. 4A. FIG. 4B shows the dependence of GO concentration on the centrifuge time at 10000 rpm.

FIG. 5 shows an exemplary fabrication process of highly selective GO membranes.

FIG. 6 shows an exemplary schematic drawing of gas permeation measurement system.

FIG. 7 shows a XRD patterns for (A) GO powder on A1 plate and (B) blank A1 plate.

FIG. 8 shows gas adsorption isotherms of CO₂, CH₄, N₂, and H₂ on GO at 20° C.

FIG. 9 shows Arrhenius temperature dependence of H₂ and CO₂ permeances in the 50/50 mixture for the 1.8-nm thick GO membrane. Gas permeance through the membrane satisfies Arrhenius dependence when adsorption is in Henry's region according to the equation:

${Permeance} \propto ^{\frac{- {({ɛ_{d} - {\Delta \; H_{ads}}})}}{RT}}$

where, E_(d) is diffusion activation energy (kJ/mol) and ΔH_(ads), is the heat of adsorption (kJ/mol). From the above figure, the calculated E_(d)−ΔH_(ads) are 6.9 kJ/mol for H₂ and 60.2 kJ/mol for CO₂, respectively. Considering much weaker adsorption of H₂ on most of porous materials than CO, heat of adsorption of CO₂ on GO is also expected to be higher than H₂. Therefore, diffusion activation energy of CO through the GO membrane is at least 53.3 kJ/mol higher than that of H₂, indicating much more activated diffusion of CO₂ through GO membranes or much tighter fit of CO₂ in defects of GO flakes.

FIG. 10 shows a comparison of ultrathin GO membranes with polymeric membranes for H₂/N₂ mixture separation: selectivity versus H₂ permeance. The line is the 2008 upper bound of polymeric membranes for H₂/N₂ and round points are representative polymeric membranes, assuming membrane thickness is 1 p.m. The circle points are representative points for polymeric membranes from literature. 1 GPU (Gas Permeance Unit) equals to 3.348×10⁻⁸ mol/(m²·s·Pa).

FIG. 11 shows a HRTEM image of a single-layer GO flake.

FIG. 12 shows a Raman spectrum of the GO powder. The ID/IG ratio is 1.09 as shown in the figure.

DETAILED DESCRIPTION

Reference now will be made to the embodiments of the invention, one or more examples of which are set forth below. Each example is provided by way of an explanation of the invention, not as a limitation of the invention. In fact, it will be apparent to those skilled in the art that various modifications and variations can be made in the invention without departing from the scope or spirit of the invention. For instance, features illustrated or described as one embodiment can be used on another embodiment to yield still a further embodiment. Thus, it is intended that the present invention cover such modifications and variations as come within the scope of the appended claims and their equivalents. It is to be understood by one of ordinary skill in the art that the present discussion is a description of exemplary embodiments only, and is not intended as limiting the broader aspects of the present invention, which broader aspects are embodied exemplary constructions.

Chemical elements are discussed in the present disclosure using their common chemical abbreviation, such as commonly found on a periodic table of elements. For example, hydrogen is represented by its common chemical abbreviation H; helium is represented by its common chemical abbreviation He; and so forth.

Methods are generally provided for the preparation of large permeation area (e.g., about 4 cm² or greater) graphene oxide (GO) membranes, along with the resulting microporous inorganic membranes and methods of their use for separation of H₂ mixtures. In one embodiment, the GO membranes are composed of about 3 to about 30 layers of GO flakes, by a facile and scalable filtration process. Compared with current microporous inorganic membranes and polymeric membranes, this new class of ultrathin GO membranes showed superior separation performance for H₂ mixtures. Ultrathin, molecular-sieving membranes have great potential to realize high flux, high selectivity gas mixture separation at low energy cost.

The method of forming such an ultrathin GO membrane can begin with a single-layered graphene oxide powder. For example, the single-layered graphene oxide powder can be dispersed into deionized water to form a single-layered graphene oxide dispersion.

The single-layered graphene oxide dispersion can then be centrifuged to remove any aggregated graphene oxide material and other large particles from the single-layered graphene oxide dispersion. For example, the single-layered graphene oxide dispersion can be centrifuged for about 30 minutes to about 40 minutes. Depending on the size of the sample, the single-layered graphene oxide dispersion can be centrifuged at speeds of about 5,000 rotations per minute (rpm) to about 15,000 rpm, such as at about 10,000 rpm.

In one particular embodiment, the single-layered graphene oxide dispersion can be sonicated to ensure substantially uniform dispersion of the single-layered graphene oxide in the deionized water. For example, the single-layered graphene oxide dispersion can be sonciated for about 15 hours or more to ensure complete dispersion of the single-layered graphene oxide flakes within the dispersion. In one particular embodiment, sonication can be performed at ultrasonic frequencies (e.g., greater than about 20 kHz). Sonication is, in one embodiment, performed after centrifuging the single-layered graphene oxide dispersion such that substantially all of the large aggregations and/or particles have already been removed. In another embodiment, the single-layered graphene oxide dispersion can be sonicated prior to centrifuging.

In one embodiment, the single-layered graphene oxide dispersion is diluted by about ten times or more through the addition of deionized water after centrifuging and, optionally, sonicating. For example, the single-layered graphene oxide dispersion can be diluted by about twenty times or more through the addition of deionized water, such as about one hundred times or more. For instance, the single-layered graphene oxide dispersion can be diluted to a concentration of about 0.2 mg/mL to about 0.4 mg/mL, such as about 0.3 mg/mL.

The diluted single-layered graphene oxide dispersion can then be passed through a substrate such that a graphene oxide membrane is formed thereon. The substrate generally defines a plurality of relatively small pores. The graphene oxide membrane can be any suitable material, such as an aluminum oxide (e.g., an anodic aluminum oxide), a cellulose acetate, etc.

In one embodiment, the substrate is supported by a filter having pores larger than the pores present in the substrate. The pores in the filter can, for instance, have a pore size of about 20 run to about 100 nm.

The graphene oxide membrane can be dried to remove any residual water present in the membrane. For example, the graphene oxide membrane can be dried by storing the graphene oxide membrane in a vacuum desiccator.

The resulting graphene oxide membrane is, in one embodiment, generally formed from a plurality of single-layered graphene oxide flakes. These single-layered graphene oxide flakes can generally form layers stacked on each other. For example, the graphene oxide membrane can be formed from about 3 to about 10 layers of single-layered graphene oxide graphene oxide flakes. In certain embodiments, the single-layered graphene oxide flakes have a size up to about 500 nm.

The graphene oxide membrane has, in particular embodiments, a thickness of about 1.8 nm to about 180 nm, such as about 1.8 nm to about 20 nm (e.g., about 1.8 nm to about 18 nm).

Examples

Ultrathin, down to around 1.8 nm in thickness, graphene oxide (GO) membranes were prepared and were found to separate small gas molecules by molecular sieving through intrinsic structural defects on GO. These membranes were prepared by a facile and scalable filtration process and showed mixture separation selectivities of 3400 and 900 for H₂/CO₂ and H₂/N₂ mixtures, respectively, and H₂ permeances as high as 2×10-7 mol/(m²·s·Pa). This new class of ultrathin, molecular-sieving membranes may have significant applications for H₂ separations, gas sensors, and seawater desalination.

It was found that centrifugation and dilution of GO dispersions are critical for preparing high quality CO) membranes. For example, 30-min centrifuge at 10000 rpm can remove most of large particles/aggregates and 25-ml is an appropriate volume for preparing high quality GO membranes thinner than 20 nm. FIG. 1A shows a about 9-nm thick GO membrane with a permeation area of about 4 cm². Yellow Kapton tape with an open hole was attached on the surface of the (GO membrane supported on an AAO filter to avoid direct contact between the sealing O-ring and the GO membrane surface. XRD shows the characteristic peak of GO at 28 of 11.1° (FIG. 7), and GO flakes are about 500 nm in size and single layered, as confirmed by the AFM image (FIG. 1B) and the height profile of a GO flake (FIG. 1C). FIGS. 1D and 1E show the surface of an 18-nm thick GO membrane on AAO. Compared with AAO support (FIG. 1F), a very thin GO coating can be clearly seen. We deposited a relatively thick GO membrane on AAO using a 25-ml GO dispersion in DI water with a known amount of GO and found its thickness is approximately 180 nm (FIG. 1G). GO dispersion for this 180-nm membrane preparation was then diluted 100, 20, and 10 times to obtain ca. 1.8-, 9-, and 18-nm thick GO membranes. X-ray photoelectron (XPS) spectroscopy was used to detect surface elements for these ultrathin GO membranes on AAO (FIGS. 1H and 1I); for 1.8-nm thick membrane, significant amount of aluminum in AAO can still be seen because mean free path of excited electrons is longer than surface GO membrane thickness, while for thicker membranes (9 and 18 nm), much smaller amounts of underlying aluminum in AAO can be seen because GO thickness is larger than excited electron mean free path. This is consistent with surface carbon detection by XPS as well (FIG. 11). See Supplementary Material for detailed analysis.

We conducted permeation of small gas molecules with different sizes to probe pore sizes in ultrathin (less than 20 nm) GO membranes. FIG. 2A shows the permeance (=flux/pressure drop) of four molecules (He, H₂, CO₂, and N₂) through an about 18-nm thick GO membrane at 20° C. Hydrogen permeated approximately 300 times faster than CO₂ and N₂ molecules, while their kinetic diameter differences are only 0.04 and 0.07 nm, respectively. This strongly suggests molecular-sieving behavior of the GO membrane; the average pore size in the GO membrane is probably smaller than a CO₂ molecule. We also made thicker GO membranes and measured their single gas permeation; for a 90-nm thick GO membrane, ideal selectivities (ratio of permeances of pure components) of H₂ over CO₂ and N₂ are as high as 1150 and greater than 1000, respectively, and H₂ permeance is 3.4×10-8 mol/(m²·s·Pa). This report, however, will focus on separation study of ultrathin GO membranes (less than 20 run thickness). FIG. 2B shows H₂ and He permeances for GO membranes with different thickness (up to 180 nm). Gas permeance is usually expected to be inversely proportional to the membrane thickness due to the proportional increase of transport resistance with thickness (23). Surprisingly, we found H₂ and He permeances decrease exponentially with the increase of membrane thickness from 1.8 to 180 nm (FIG. 2B). We speculate major transport pathway for these molecules are structural defects on GO flakes, instead of spacing between GO flakes. Exponential dependence of H₂ and He permeances may result from the particular transport pathway of molecules through these structural defects in layered GO membranes. Various defects on graphene, such as line defect missing octagons passivated by hydrogen, nitrogen-functionalized pores, and other artificially drilled holes, have been found to be able to separate H₂ from other small molecules (N₂, CH₄ etc.). Intrinsic defects on GO flakes in our membranes may be attributed to molecular-sieving behavior of H₂ over other molecules. Koenig et al. found molecular-sieving behavior of porous graphene after UV-induced oxidative etching; H₂/N₂ ideal selectivity was higher than 10000 after etching. We noticed that some of their graphene sheets before etching showed high ideal selectivities for H₂/CH₄ (about 100) and H₂/N₂ (about 100), indicating intrinsic defects on graphene may also have decent molecular-sieving behavior. Their finding is consistent with our single-gas permeation results. Recently, Nair et al. prepared about 1 μm thick GO membranes using GO flakes and found that even helium can't permeate through (permeance<2.5×10-14 mol/m²·s·Pa). If we extrapolate He permeance for 1 μm thick GO membrane using exponential fit in FIG. 2B, its permeance would be appropriately 10-16 mol/m²·s·Pa. This is consistent with Nair et al. finding. Therefore, for practical separation application of GO membranes, ultrathin thickness is essential in order to have reasonable gas permeances.

Separation of H₂ from other small molecules has important applications for pre-combustion CO₂ capture, H₂ recovery for ammonia production, and natural gas upgrading. Separation selectivity, defined as the ratio of component permeances in mixtures, and permeance are two important parameters to evaluate membrane separation performance. Before evaluating separation performance of ultrathin GO membranes, a control experiment was first conducted to measure separation performance of an AAO support, and we found that permeances of studied gases were high (greater than 10⁻⁶ mol/(m²·s·Pa)) and selectivitis of H₂ over CO₂ and N₂ were low (less than 5), as expected for Knudsen diffusion through 20 nm pores. We then performed 50/50 H₂/CO₂ and H₂/N₂ mixture separation from 20 to 100° C. for GO membranes with thickness from 1.8 to 18 nm. FIG. 3 shows separation results for 1.8-, 9-, and 18-nm thick GO membranes. All the GO membranes showed extremely high H₂/CO₂ selectivity (greater than 2000) at 20° C., with the highest of 3400 for the 9-nm thick membrane. This is unusual, because previous microporous membranes either showed low H₂/CO₂ selectivity or reversely selected CO₂ over H₂ at room temperature or lower temperatures due to strong adsorption of CO₂ in pores and thus blocking of H₂ permeation. We measured adsorption isotherms of CO₂, CH₄, N₂, and H₂ on GO powder and found that indeed CO₂ adsorbs much more strongly than H₂ on GO powder (FIG. 8). These results strongly suggest that true molecular-sieving separation of H₂ from CO₂ is achieved, because strongly adsorbed CO₂ on GO flakes has negligible effects on H₂ permeation, meaning CO₂ can't enter most of the structural defects on GO that are only for H₂ permeation. CO₂ seems to permeate through very small amount of larger structural defects that allow both CO₂ and H₂ permeation, and these larger defects are also selective for H₂ over CO₂, probably due to smaller size of H₂. This may explain higher H₂/CO₂ separation selectivity than ideal selectivity. H₂/CO₂ separation selectivity decreased with the increase of temperature, resulting from the faster increase of CO₂ permeance than that of H₂. But, at even 100° C., H₂/CO₂ selectivity is still 250 for the 18 nm thick membrane. This suggests a more activated CO₂ diffusion than H₂ through GO membranes, resulting from the tight fit of CO₂ molecules in these defects. H₂/N₂ mixture separation showed similar behavior, and the highest selectivity is approximately 900 for 9 nm GO membrane at 20° C. We prepared multiple GO membranes for each thickness and obtained good reproducibility; variation of membrane permeation performance is within 15% for all membranes, resulting from simple and highly controllable GO membrane deposition process. We also deposited ultrathin GO membranes on low-cost isopore cellulous acetate support (100 nm pores) and found similar separation performance; for example, for an approximately 18 nm thick GO membrane on cellulous acetate support, H₂/CO₂ and H₂/N₂ separation selectivities are 1112 and 300, respectively, with H₂ permeance of approximately 1.6×10-7 mol/(m²·s·Pa). This suggests that ultrathin GO membrane preparation method is applicable to both inorganic supports and polymeric supports and indicates great commercialization potential for (K) membrane preparation method. FIG. 3E shows a comparison of ultrathin GO membranes with polymeric membranes and inorganic membranes for H₂/CO₂ mixture separation. Typically, for membrane separation, with the increase of separation selectivity, permeance decreases. An upper bound can usually be used to compare the separation performance of a new membrane with previous membranes. Ultrathin GO membranes are far beyond the upper bounds for both polymeric membranes (lower line) and representative inorganic membranes (upper line). Therefore, ultrathin GO membranes clearly represent a great breakthrough for H₂/CO₂ mixture separation by membranes. FIG. 10 also shows the comparison of GO membranes with polymeric membranes for H₂/N₂ mixture separation; superior separation performance of GO membranes can also be seen. These mixture separation results indicate the great potential of the ultrathin GO membranes for molecular-sieving separation of H₂ from other small molecules and may have significant applications on industrially important H₂ separation processes.

Graphene Oxide (GO) Membrane Fabrication

Single-layered graphene oxide (SLGO) powder, prepared by the Modified Hummer's Method, were used as the raw material for membrane preparation. In an attempt to examine the commercialization potential of our membrane preparation process, a large quantity of SLGO was purchased from CheapTubes.com (greater than Igram), instead of preparing small quantity in our lab; 1 gram of SLGO powder is enough to prepare a total membrane area of greater than 50 m², assuming a membrane thickness of 10 nm and a membrane density similar to graphite. Firstly, SLGO powder was dissolved in DI water, followed by a 25 min sonication. Then, the dispersed SLGO powder was centrifuged at 10000 rpm for different times (Bio Lion XC-H165) to remove large particles/aggregates in the dispersion. This step is critical for preparing high quality membranes. The concentration of the resulting SLGO solution was measured by UV-vis (Shimadzu UV-2010PC) with a pre-calibrated curve of GO concentration vs. absorption at 600 nm wavelength, as shown in FIG. Sla. The effects of the centrifuge time on final SLGO concentration was investigated, and it was found that 30 and 40 min gave the same concentration, as shown in FIG. 4B. So, for membrane fabrication, SLGO dispersion was used after 30 min centrifuge. During fabricating GO membranes, the SLGO dispersion was used to do vacuum filtration (Millipore filtration system) through anodic aluminum oxide (AAO) filters with 20-nm pores (Whatman) or isopore cellulous acetate with 100-nm pores (Millipore). To roughly control the GO membrane thickness, the effective filtration area was calculated, and the known amount of GO was added in its 25-ml dispersion for filtration, assuming the membrane density is similar to that of graphite (about 2.1 g/cm³). The actual thickness of a thick GO membrane with known amount of GO was measured by FE-SEM (FIG. 1G) and used to calculate thickness of thinner GO membranes with much smaller amount of GO. The resulting GO membranes were stored in a vacuum desiccator (Nalgene) for about 15 hours to remove the residue water before permeation test. A schematic process of the fabrication steps is shown in FIG. 5.

Permeation/Separation Experimental Setup

A glass membrane module was used for gas permeation/separation experiments. Silicon O-rings were used to seal the GO membranes on AAO supports or cellulous acetate supports. To avoid direct contact between O-rings and the GO membrane and thus potential damage on the thin GO membranes heat resistant Kapton tape was attached with a hole on the GO membranes to expose the desired membrane area for gas permeation; a coarse filter paper (Fisher Scientific) was placed at the bottom of the AAO or cellulose acetate support to protect the support. During permeation test, feed flow was either pure gasses or gas mixtures and their composition and total flow rate were controlled by Mass Flow Controllers (Brooks 5850); on the permeate side, argon was used as a sweep gas to bring permeates into a gas chromatography (GC) for composition analysis. The reason argon was used as the sweep gas is because argon was used as the carrier gas in GC for a better detection of H₂ by thermal conductivity detector (TCD) due to their large thermal conductivity difference. Nitrogen was detected by TCI), CH₄ and CO₂ were detected by both TCI) and flame ionization detector (FID) (CO₂ as CH₄ by a methanizer). Typically, total feed flow rates were 45 sccm for single-gas permeation and 90 sccm for mixture separation, and permeate argon flow rate was 25 sccm. A low pressure drop (about 10 kPa) or no pressure drop across the membranes was applied to avoid breaking or deforming the thin supports: for low pressure drop, the feed outlet gas tubing was plugged underneath a certain depth of water to control the feed pressure. It was found that permeances for both single gases and gas mixtures were similar with and without pressure drop. Therefore, only data collected without pressure drop were reported here. A heating tape was used to heat the membrane and a temperature controller was used to control the membrane temperature, if needed. The schematic for the permeation setup is shown in FIG. 6.

Characterization

#1 X-Ray Diffraction (XRD) Study of the GO Powder:

X-ray powder diffraction (XRD) was carried out using a Rigaku MiniFlex II diffractometer with Cu Kα radiation (λ=0.15418 nm). The diffraction data was recorded for 2θ angles between 5° and 60°. XRD pattern for the GO powder was shown in FIG. 7. The characteristic diffraction peak (002) of GO is ascribed to the introduction of oxygenated functional groups, such as epoxy, hydroxyl (—OH), carboxyl (—COOH) and carbonyl (—C═O) groups attached on both sides and edges of carbon sheets.

#2 X-ray photoelectron spectroscopy (XPS) analysis of GO membranes The surface chemical compositions of GO membranes with different thickness (1, 8, 9 and 18 nm) was analyzed by XPS (Kratos Axis Ultra DLD instrument equipped with a monochromated A1 Ka x-ray source and hemispherical analyzer capable of an energy resolution of 0.5 eV), as shown in FIG. 1H and FIG. 1I. The A1 2p peak appears near 74.3. For C is, 284.5 eV corresponds to the C≡C, C≡C and C—H bonds. 286.5 eV and 288.3 eV are assigned to C—O and C═O, respectively. We calculate the kinetic energy for A1 2p electrons with the equation Ekinetic=EX-ray photon—Ebinding—Φ, where EX-ray photon is 1486.7 eV for A1 Ka x-ray source, Ebinding for A1 2p electrons is 74.3 eV as shown in FIG. 1(H), and the working function Φ is 4.26 eV. Thus, the kinetic energy for A1 2p electrons is 1408.14 eV. By applying the dependence of inelastic mean free path (IMFP) for electrons on their kinetic energy (35), we get the λIMFP around 3.4 nm, which is larger than the thickness of our 1.8 nm GO membrane. Similarly, for C 1 s electrons, λIMFP in carbon is approximately 3 nm, which is smaller than the thickness of both 9 and 18 nm GO membrane. This is why as the membrane thickness increases, C 1 s peak intensity increases, while A1 2P peak intensity decreases, and for 9 and 18 nm GO membranes on AAO, A1 2p and C is spectra are similar.

#3 Atomic Force Microscopy (AFM) Study of GO Flakes

To prepare samples for AFM imaging, 0.002 mg/mL GO suspensions were first diluted 1000 times. A 4 uL drop of diluted suspension was deposited onto freshly cleaved muscovite mica disks (9.9 mm diameter, Grade V1, Structure Probe, Inc.) and dried for at least 20 mins at 323K prior to AFM imaging. The deposited GO sheets were imaged using a PicoPlus AFM (Agilent) operated in the tapping mode. All images were collected using N-type silicon cantilevers (FORTA-50, Nanoscience Instruments, Inc.) with spring constants of 1.2-6.4 N/m, resonance frequencies of 47-76 kHz, and nominal tip radius of <10 nm. The height resolution of the AFM scanner is less than 1 A. Thus, with proper calibration, the accuracy of the measured height of surface features is approximately ±0.1 nm. The AFM topography images were analyzed using image analysis software (Scanning Probe Image Processor or SPIP, Image Metrology A/S, Denmark), as shown in FIG. 1B. It is seen that the GO sheet is a typical single-layer GO flake with a dimension of 300-700 nm. The GO flake showed a smooth planar structure. The height profile diagram FIG. 1C of the AFM image showed that the thickness of the single-layer GO sheet was 0.7-0.9 nm, which is in coordinance with the 0.8 nm as the typical thickness of the observed single-layer GO.

#4 Field Emission Scanning Electron Microscopy (FE-SEM) Study of the GO Membranes

FIG. 1E-F shows the FE-SEM (Zeiss Ultraplus Thermal Field Emission Scanning Electron Microscope) images for blank AAO and 18 nm GO membranes coated on AAO, respectively. The difference between coated and uncoated AAO can be easily noticed that for uncoated AAO, there are 20 nm pores all around the surface dispersed uniformly, while for the coated AAO with thin layers of GO on the top, the AAO intrinsic 20 nm pores are covered by GO layers. A cross-section image for our 180 nm thick GO membrane on AAO support is shown in FIG. 1G.

#5 Gas Adsorption Isotherms Study on GO Powder

Adsorption isotherms of CO₂, CH₄, N₂, and H₂ on GO powder were measured by a volumetric method using a home-built adsorption system. GO powder (about 0.5 g) was firstly outgassed at 80-100° C. overnight. Helium was then used to calibrate the volume of adsorption cell with GO powder at 20° C. After vacuum to remove residue gasses in the adsorption system, interested gases were introduced at 20° C. to measure the adsorption isotherms on GO. The operating pressure range is from 0 to 170 kPa.

#6 High-Resolution Transmission Electron Microscopy (HRTEM) Study of the GO Flakes

To find out the defects on the single-layer GO sheets, we conducted HRTEM (JEOL JEM 2100F HRTEM). FIG. 11 shows a HR-TEM of a GO flake. Under the current resolution, no conclusive evidence shows obvious defects on GO flakes, although Raman spectrum suggests the existence of defects on GO (see analysis below). #7 Raman spectroscopy analysis of GO powder To further study the structural properties of the GO powder, we conducted Raman spectroscopy. A LabRam confocal Raman spectrometer (JY Horiba) is used for the measurement. The spectrometer is equipped with a liquid-nitrogen cooled, charged coupled device (CCD) detector, and a He—Ne (632.817 nm) laser for excitation. The well-known Raman characteristics of carbon materials are the G and D bands (1580 and 1350 cm⁻¹) which are usually assigned to the graphitized structure and local defects/disorders particularly located at the edges of graphene and graphite platelets. Therefore, a smaller ID/IG peak intensity ratio can be assigned to lower defects/disorders in the graphitized structure. The Raman spectrum shown in FIG. 12 display the G band at 1585 cm⁻¹ and the D band at 1338 cm⁻¹. The values of the ID/IG ratio were also obtained and presented in FIG. 12. A methodology to correlate the ID/IG ratio with the distance between pointlike defects (LD) on single layer graphene (SLG), focusing on the low-defect density regime (LD≧10 nm), is shown in the following equation:

${L_{D}^{2}\left( {nm}^{2} \right)} = {\frac{\left( {4.3 \pm 1.3} \right) \times 10^{3}}{E_{L}^{4}}\left( \frac{I_{D}}{I_{G}} \right)^{- 1}}$

By substitute ID/IG=1.09 and EL=1.96 eV for the He—Ne (632.817 nm) laser into this equation, we can get the LD between 13.6 to 18.6 nm, assuming this dependence of ID/IG on LD can also be applied to SLGO. The detailed derivation of this equation can be found in references.

In summary, ultrathin GO membranes, down to about 1.8 nm in thickness, which is the thinnest gas separation membranes so far, were prepared by a facile, highly repeatable, and scalable filtration deposition process. Ultrathin GO membranes can be deposited on both inorganic porous supports and low-cost polymeric supports, indicating generality of the membrane preparation method and great potential for commercialization. A very small amount of GO per area, resulting from the ultrathin membrane thickness, also makes this material low cost for preparing large area separation membranes. This new class of ultrathin GO membranes showed molecular-sieving separation behavior for H₂ mixtures; unprecedented H₂/CO₂ separation selectivities, e.g., greater than 3000, were obtained, and H₂/N₂ mixture separation selectivities can be as high as 900, for membranes thinner than 20 nm. These results indicate the great potential of these ultrathin GO membranes for industrially important H₂ separations and may have wide applications, including but not limited to, gas sensors and for seawater desalination.

These and other modifications and variations to the present invention may be practiced by those of ordinary skill in the art, without departing from the spirit and scope of the present invention, which is more particularly set forth in the appended claims. In addition, it should be understood the aspects of the various embodiments may be interchanged both in whole or in part. Furthermore, those of ordinary skill in the art will appreciate that the foregoing description is by way of example only, and is not intended to limit the invention so further described in the appended claims. 

What is claimed:
 1. A filtration membrane, comprising: a graphene oxide membrane having a thickness of about 1.8 nm to about 180 nm, wherein the graphene oxide membrane comprises about 3 to about 30 layers of single-layered graphene oxide flakes.
 2. The filtration membrane of claim 1, wherein the single-layered graphene oxide flakes have a size up to about 500 nm.
 3. The filtration membrane of claim 1, wherein the graphene oxide membrane has a thickness of about 1.8 nm to about 20 nm.
 4. The filtration membrane of claim 1, wherein the graphene oxide membrane has a thickness of about 1.8 nm to about 18 nm.
 5. The filtration membrane of claim 1, wherein the graphene oxide membrane comprises about 3 to about 10 layers of the single-layered graphene oxide flakes.
 6. The filtration membrane of claim 1, wherein the graphene oxide membrane has an area of about 4 cm² or greater. 